超细矿渣粉对硅酸盐水泥性能和微观结构的影响

通过掺入不同量的超细矿渣粉,研究其对普通硅酸盐水泥凝结时间、标准稠度用水量以及水泥胶砂流动性和强度的影响。结果表明,水泥浆体的初凝、终凝时间在矿渣粉掺量为5%(质量分数,下同)时有所缩短,而随着超细矿渣粉掺量的增加,初凝时间都有所延长,在掺量为20%时初凝时间最长。然而终凝时间的变化不大,只有掺量为30%时稍有延长;水泥的标准稠度用水量先减少后增加,在掺量为20%时最小;随着超细矿渣粉掺量的增大,水泥胶砂的各龄期抗折强度、3d抗压强度不断提高,7d、28d抗压强度在掺量为20%时达到最大值,之后有所降低。掺入超细矿渣粉后,能通过填充以及与水泥水化产物氢氧化钙发生反应,使水泥中氢氧化钙含量明显降低,水泥微观结构更加密实。     

普通硅酸盐-硫铝酸盐水泥复合凝胶体系的制备及性能研究

根据设计配比,制备了普通硅酸盐-硫铝酸盐水泥复合凝胶体系。通过改变普通硅酸盐水泥和硫铝酸盐水泥的质量比、水胶比和减水剂用量等参数,采用净浆流动度、凝胶时间、结石率、抗压强度和竖向膨胀率等实验,探究了普通硅酸盐-硫铝酸盐水泥复合凝胶体系的性能影响因素。结果表明,当硫铝酸盐水泥的用量为70%(质量分数)、水胶比为0.5、减水剂用量为0.5‰(质量分数)时,复合胶凝体系的流动度最大,达320 mm,可注性好;其初凝和终凝时间分别为6和14 min,凝胶时间短;其结石率为100%,28 d竖向膨胀率约为0.14%,无需二次注浆;其28 d抗压强度为43 MPa,加固强度高。适量的硅灰和硅渣的掺杂可以提高复合胶凝体系后期的抗压强度、抗折强度和流动度,当硅灰掺量为10%(质量分数)时,复合胶凝体系3和28 d的抗压强度、抗折强度出现了峰值;当硅渣掺量为15%(质量分数)时,复合胶凝体系28 d的抗压强度和抗折强度达到最高;当硅渣掺量为10%(质量分数)时,复合胶凝体系流动度达到334 mm。     

水泥对石膏基自流平材料性能的影响

研究了硅酸盐水泥和铝酸盐水泥对石膏基自流平材料流动度、凝结时间、力学性能和耐水性能的影响,通过X射线衍射仪、量热仪、压汞仪和环境扫描电子显微镜微观测试方法对水化产物、水化热、孔结构、微观形貌等进行分析表征。结果表明,随着硅酸盐水泥掺量的增加,初始流动度增大,30min流动度损失减小,凝结时间缩短,掺加铝酸盐水泥对流动度、凝结时间规律与硅酸盐水泥相似;随着硅酸盐水泥掺量的增加,力学性能和耐水性能呈先增加后降低趋势,当掺量为8%时,达到最优;28d抗折强度和耐水性能随着铝酸盐水泥掺量的增加,波动比较大,在13%掺量时出现最低点,抗压强度随着铝酸盐水泥掺量的增加呈稳步上升趋势;掺入硅酸盐水泥和铝酸盐水泥均出现钙矾石的微弱衍射峰。     

硫铝酸盐水泥基高性能混凝土的制备及性能研究

采用硫铝酸盐水泥,根据设计配比,配制了硫铝酸盐水泥基高性能混凝土,探究了硫铝酸盐水泥不同掺量(0,3%,6%和9%(质量分数))对高性能混凝土力学性能(抗压强度)和耐久性能(侵蚀性)的影响。通过XRD、SEM、热分析和力学性能分析等对硫铝酸盐水泥基高性能混凝土进行了表征。结果表明,随着硫铝酸盐水泥掺量的增加,钙矾石(AFt)的衍射峰逐渐增强,水化反应加快,高性能混凝土的结构变得更加致密;所有试样中的六方板状的Ca(OH)_2均比较厚,且呈现出片层状,整体结构的致密性比较接近,而随着硫铝酸盐水泥掺量的增加,整体的密度有变得蓬松的趋势;随着硫铝酸盐水泥掺量的增加,CH的含量增加,前期的水化放热能力得到提高,所有试样在3和28 d时的抗压强度均呈现出逐渐增大的趋势,当硫铝酸盐水泥的掺量为9%时,试样的抗压强度在28 d达到了最大值41.1 MPa,相比3 d增加了19.83%;随着硫铝酸盐水泥掺量的增加,高性能混凝土试样的强度损失逐渐增加,耐久性变差,当硫铝酸盐水泥的掺量为9%时,腐蚀90 d的强度损失率达到了最大值10.3%。     

高性能硫铝酸盐-硅酸盐复合胶凝体系的制备及性能研究

根据实验配比,制备了硫铝酸盐-硅酸盐复合胶凝体系,通过XRD、SEM、TG-DTG和力学性能分析等对复合胶凝体系进行了表征,探究了不同硫铝酸盐掺量下复合胶凝体系的物相结构、显微形貌、热性能和力学性能。结果表明,硫铝酸盐-硅酸盐复合胶凝体系中主要检测到Ca(OH)_2、Mulite、钙矾石(AFT)、水硫铝钙石(Kuzelite)、单硫型硫铝酸钙(AFm)和Ca_3SiO_5等产物相,随着硫铝酸盐掺量的增加,体系水化产物中Ca(OH)_2的峰均有降低趋势;不同硫铝酸盐掺量的复合胶凝体系的结构致密性相差不大,随着硫铝酸盐掺量的增加,大量针状的钙矾石(AFT)的含量明显增加,块状的Ca_3SiO_5含量减少;所有复合胶凝体系的失重曲线规律较为相似,且掺杂硫铝酸盐水泥的体系的失重率均明显高于不掺杂的试样;随着硫铝酸盐掺量的增加,复合胶凝体系在1,3和28 d的抗压强度均呈现逐渐增大的趋势,当硫铝酸盐的掺量为25%(质量分数)时,复合胶凝体系在28 d的抗压强度达到了最大值49.3 MPa,相比在1 d时36.5 MPa,增加了35.1%。     

基于溶胶凝胶法改性的硅藻土对水泥基材料性能的影响

采用溶胶凝胶法对硅藻土进行改性,然后研究改性前后的硅藻土对水泥净浆(标准稠度用水量、凝结时间)及砂浆性能(力学性能、调湿性能)的影响。研究结果表明:(1)经改性后的硅藻土比表面积由初始的2.76m~2/g增大到158.52m~2/g,平均孔径由初始的3.82nm减小到1.41nm。(2)改性前后的硅藻土水泥净浆标准稠度用水量均高于纯水泥的标准稠度用水量,且随着硅藻土掺量的增加而逐渐增大;随着改性前后硅藻土掺量的增加,水泥初凝时间延长,终凝时间缩短。另外,在硅藻土掺量相同的条件下,改性硅藻土时凝结时间较原状硅藻土水泥凝结时间短。(3)改性后硅藻土的水泥砂浆强度较原状硅藻土的水泥砂浆高;随着改性前后硅藻土掺量的增加,水泥砂浆的强度均逐渐降低,而水泥砂浆吸、放湿率逐渐增大。另外,改性前后的硅藻土掺量相同时,改性后硅藻土的水泥砂浆吸、放湿率大于改性前的硅藻土水泥砂浆的吸、放湿率。(4)X射线衍射(XRD)和扫描电镜(SEM)分析结果表明,改性硅藻土的水泥砂浆较原状硅藻土的水泥砂浆有更多的水化产物,且硬化体结构更加致密。     

硫铝酸盐水泥和丁苯乳液对水泥基修补材料性能的影响

将硫铝酸盐水泥与硅酸盐水泥复合,并引入丁苯乳液作为聚合物改性剂制备高性能修补材料,研究硫铝酸盐水泥和丁苯乳液对修补材料的强度、凝结时间和黏度的影响和作用机制。结果表明:硫铝酸盐水泥明显提高复合水泥的早期强度,缩短初凝和终凝时间,增大黏度;适量丁苯乳液能在复合水泥浆体中形成网状结构,提高力学强度;丁苯乳液中的羧基能够减小熟料矿物铝酸钙、硅酸三钙和硅酸二钙的水化速率,复合水泥净浆的初凝和终凝时间均明显延长,黏度减小。     

Cr~(3+)、Pb~(2+)在不同水泥水化体系中的固化

研究了重金属离子Cr~(3+)和Pb~(2+)对硅酸盐水泥、硫铝酸盐水泥及混掺水泥(普通硅酸盐水泥与硫铝酸盐水泥进行混掺)三种水泥的浆体凝结时间和力学性能的影响,并借助X射线衍射技术(XRD)和电感耦合等离子体发射光谱(ICP)等研究了水泥水化产物特征、重金属元素在水泥浆体中的固化方式与溶出特性。结果表明:Cr~(3+)对三种水泥均产生促凝作用,而Pb~(2+)对普通硅酸盐水泥和混掺水泥产生缓凝作用,对硫铝酸盐水泥产生促凝作用。Cr~(3+)和Pb~(2+)的掺加引起AFt和Ca(OH)_2形成量的变化,影响程度与水泥品种有关,掺加Cr~(3+)的28d浆体中有新相Ca_2Cr(OH)_7·3H_2O生成。所研究的三种水泥中,硅酸盐水泥对Cr~(3+)的固化效果最好,当Cr~(3+)掺量为1%时,其Cr~(3+)浸出浓度仅为0.177mg/L;而硫铝酸盐水泥对Pb~(2+)的固化效果最好,当Pb~(2+)掺量为1%时,其Pb~(2+)浸出浓度仅为0.0064mg/L。     

聚羧酸减水剂对硫铝酸盐水泥水化及硬化的影响

为研究聚羧酸减水剂(PCE)对硫铝酸盐水泥(SAC)水化及硬化的影响,本工作以PCE对SAC标准稠度用水量、初始流动度、经时损失、粘度、凝结时间以及强度的影响进行了试验,同时测试了PCE对SAC浆体的水化温升以及水化产物的影响。结果表明:PCE在SAC浆体中的最佳掺量为0. 4%,减水率可达33%以上,初始流动度可达375 mm以上,初凝与终凝时间分别由24 min和36 min延至117 min和129 min。PCE对SAC浆体的流动度改善明显,并产生一定的缓凝作用。PCE掺量在0. 2%～0. 4%范围内,早期强度发展缓慢,但不影响其后期强度的增长。PCE掺量为0. 4%时,7 d抗压强度达102 MPa,抗折强度达11. 6 MPa。相比对照组,7 d抗压强度提高41. 8%,抗折强度提高20. 8%。     

调凝剂对物理发泡水泥性能的影响

采用物理发泡制备泡沫混凝土,以普通硅酸盐水泥为基材,为了让其凝结时间与泡沫的稳定时间相匹配,研究采用硫酸铝与快硬硫铝酸盐水泥作为调凝剂以调整普通硅酸盐水泥凝结时间。研究发现:随着调凝剂(Al2(SO4)3·18H2O和快硬硫铝酸盐水泥)掺量的逐渐增加,普通硅酸盐水泥净浆凝结时间逐渐缩短,泡沫混凝土容重呈降低趋势,并且气孔尺寸逐渐减小;调凝剂的掺加会提高低容重(425Kg/m3)泡沫混凝土的早期强度,而使其后期(28d)强度有所降低;但是,随着调凝剂掺量的逐渐增加,高容重(725Kg/m3)泡沫混凝土的抗压强度逐渐降低;并用XRD方法对其水化产物进行表征,并分析了调凝剂促凝和后期强度降低的原因。结果表明:在低容重泡沫混凝土的制备过程中可以适当掺加调凝剂,而在高容重泡沫混凝土的制备过程中应避免调凝剂的使用。     

Thermoluminescence of cement

Cement is found to be a thermoluminescent material. The glow curves of ordinary portland cement obtained from two different sources are found to be qualitatively similar. White cement (J K Brand) exhibits intense thermoluminescence (TL) compared to Birla white brand. The emission of J K white cement seems to be mainly due to Mn impurities which enters the product through limestone, the major ingredient in the preparation of cement. The possible use of TL as a spectroscopic technique to characterize cement is discussed.     

Energy and cement quality optimization of a cement grinding circuit

This study aimed at optimizing both the energy efficiency and the quality of the end product by modifying the existing flowsheet of the cement grinding circuit. As a general application, mill filter stream is sent to the air classifier owing to its coarser size distribution than the desired product. However, the study proved that some further evaluations i.e., quality tests and chemical assays, could make it possible to treat this stream as a final product. Consequently, directing this stream to the final product silo could be considered. Within the study, sampling survey was undertaken initially that was followed by the modelling and simulation works. The calculations implied that the production rate increased by 4.45% that corresponded to energy saving of 4.26%. As the plant decided to change the flow sheet, another sampling campaign was arranged to validate the outputs of the simulation studies. In that case, the real data showed that the increase in production rate was 3.68% and 28-Days strength of the cement improved by 2.9%. As a result, the simulation outputs were found to be in agreement with the real data hence the efficiency of the cement production, both quality and energy, for a given circuit was improved.     

Heat deformations of cement paste phases and the microstructure of cement paste

The paper presents the results of an experimental investigation of the influence of thermal deformations of phases present in hardened cement paste on its microstructure. For the observation of the thermal deformation course in the range of temperature20–800°C, a method of complex thermal analysis (DTA, DTD, TD) was employed. The microstructure of heated cement pastes was observed by both optic and electron microscopes. From an analysis of the results of the investigation it has been found that chemical processes stimulated by temperature in particular phases of cement paste have a significant influence on the thermal deformation course. It is shown that micracracks caused by different thermal deformations, appear first in the aregas of Ca (OH)₂ concentration (ca.300°C), and next (ca.400°C) as well as in the areas of occurrence of unhydrated large clinker grains.

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Résumé On rend compte d'une étude expérimentale sur les causes de la destruction de la microstructure de la pate de ciment portland exposée à la chaleur dans une gamme de températures allant de20 à800°C. On a prêté une attention particulière aux déformations thermiques de chacune des phases reconnues de la pate de ciment durci. On a utilisé une méthode d'analyse thermique complexe (DTA, TD, DTD) pour l'étude de l'évolution de déformations thermiques. On a observé les microstructures de la pate de ciment chauffée au microscope optique et électronique. On a étudié les phases suivantes de la pate de ciment: clinkers (C₃S, β-C₂S, C₃A, C₄AF), minéraux hydratés de ciment (hydrates C₃S, β-C₂S, C₃A, C₄AF), et produits d'hydratation [Ca(OH)₂, ettringite]. Les résultats de l'étude ont permis à l'auteur de déterminer l'allure de la déformation thermique des phases que présente la pate de ciment durcie sous températures croissantes. On a constaté que les processus chimiques que l'élévation de température induit dans chacune des phases de la pate de ciment exercent une influence notable sur l'évolution des déformations thermiques. Les microfissures causées par différentes déformations thermiques des phases apparaissent dans les zones de concentralisation de Ca(OH)₂ à environ300 et400°C aussi bien que dans les zones où se rencontrent des grains de clinker non hydraté.

     

Strengthening of cement foams

Lightweight cellular concretes are attractive building materials for a number of reasons: they offer a unique combination of moderate thermal insulation and stiffness, low cost and incombustibility. They have relatively low strength, however, and are brittle. In this paper we describe the behaviour of composite cement/polystyrene foams with improved strength and ductility.     

Stability of macrodefect-free cement

Abstract

The effect of water immersion on the strength and dimension stability of macrodefect-free (MDF) cement has been studied. The results show that the polymer phase in the MDF matrix is unstable in water. Prolonged immersion resulted in substantial expansion and leaching of the matrix. Microstructural changes were examined by scanning electron microscopy, X-ray diffraction, and infrared spectroscopy. The cause of weakening of the matrix is thought to be the modification of the cement/polymer interface through the hydration of anhydrous grains. Methods of improving the performance of MDF pastes in water have been considered.

MST/692     

Free and combined chloride in hydrating cement and cement components

Normal portland cement, low C₃A cement, tricalcium silicate, and C₃A—gypsum mixtures are hydrated in the presence of 0, 0.8, 1.5 and 3.0% CaCl₂ for 1, 3, 7, 14 and 28 days and the amounts of extractable chloride determined by applying a pressure of 80 000 lb (449 MPa) or by treating the pastes with excess water. At early periods of hydration both methods yielded similar values for immobilized chloride. The amount of free chloride in the pore solution increased as the dosage of initially added chloride was increased. The C₃A—gypsum mixture immobilized much higher amounts of chloride than did the C₃S phase. Normal portland cement had lower amounts of free chloride than low C₃A cement.

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Résumé Du ciment Portland normal, du ciment CAP, du silicate tri-calcique et des mélanges de C₃A-platre sont hydratés en présence de 0, 0,8, 1,5 et 3% de CaCl₂ en 1, 3, 7, 14 et 28 jours; les quantités de chlorure que l'on peut extraire sont déterminées par application d'une pression de 449 MPa ou par traitement des pates avec un excès d'eau. Dans les premiers temps de l'hydratation les deux méthodes donnent des quantités voisines de chlorure retenu. La quantité de chlorure libre dans la solution interstitielle augmente avec le dosage de chlorure initialement ajouté. Le mélange de C₃A-platre retient des quantités beaucoup plus grandes de chlorure que ne le fait la phase C₃S. Le ciment Portland normal montre des quantités plus faibles de chlorure libre que le ciment CAP.

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This paper is a contribution from the Division of Building Research, National Research Council of Canada, and is published with the approval of the Director of the Division.     

Susceptibility of Portland cement and blended cement concretes to plastic shrinkage cracking

The market share of different types of blended cements is increasing year by year. Generally, blended cements are ground to higher fineness and exhibit a slower development of mechanical properties compared to Ordinary Portland Cement (OPC), which might affect the concrete performance in terms of shrinkage cracking at early ages.In this paper, the performance of concretes made with different cement types is compared according to the ASTM C1579-13 standard for plastic shrinkage cracking. The cracking behavior was further correlated to the deformations of both unrestrained and restrained specimens measured by a 3D image correlation system. The main factors influencing the cracking behavior were discussed based on poromechanics. It is concluded that the bulk modulus evolution has a dominant effect on controlling the plastic shrinkage cracking. Concretes made of more reactive cements, in particular with higher clinker content, are less susceptible to plastic shrinkage cracking. For cements with the same clinker content, increasing the cement fineness reduces the risk of plastic shrinkage cracking.     

Rubber-modified bone cement

A precursor rubber-toughened polymethyl-methacrylate (PMMA) powder developed by ball-milling was incorporated into a series of test bone cements, with different combinations of PMMA powder, rubber-toughened PMMA powder, MMA monomer and benzoyl peroxide (BPO) initiator. The resulting microstructures were characterized by electron microscopy and measurements made of the tensile properties, fracture mechanics parameters and curing features. It is demonstrated that rubber-toughened PMMA powder additions give a significant increase in elongation and fracture toughness, with a reduction in setting time.     

Carbon fibre-reinforced cement

This review describes fabrication processes for aligned fibre and random fibre carbonreinforced cement and links important process parameters with composite theory. The way in which the material fits into the general framework of crack constraint and matrix cracking theories is discussed. A broad survey is made of the mechanical properties, durability and dimensional stability of a variety of carbon-reinforced cement composites, and economic constraints on potential applications are considered.List of symbols b breadth of three-point bend specimen - d depth of three-point bend specimen - E _c composite Young's modulus - E _f fibre Young's modulus - E _m matrix Young's modulus - l fibre length - l _c fibre critical transfer length - l _s specimen span in three-point bend test - m Weibull modulus - r fibre radius - P applied load - V _f fibre volume fraction - V _m matrix volume fraction - x length of fibre needed to transfer load _mu V _m - x _d crack spacing in a composite with short, aligned fibres - _fu fibre ultimate strain - _mu matrix ultimate strain - _fu fibre ultimate strength - _mu matrix ultimate strength - _cu composite ultimate strength - _MOR modulus of rupture - _T tensile strength - interlaminar shear strength - _i interfacial shear strength - _m matrix work of fracture - _F work of fracture